WO2004097058A1 - ディスクブレーキ用マルテンサイト系ステンレス鋼 - Google Patents
ディスクブレーキ用マルテンサイト系ステンレス鋼 Download PDFInfo
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- WO2004097058A1 WO2004097058A1 PCT/JP2004/005934 JP2004005934W WO2004097058A1 WO 2004097058 A1 WO2004097058 A1 WO 2004097058A1 JP 2004005934 W JP2004005934 W JP 2004005934W WO 2004097058 A1 WO2004097058 A1 WO 2004097058A1
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- stainless steel
- martensitic stainless
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Classifications
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D65/00—Parts or details
- F16D65/02—Braking members; Mounting thereof
- F16D65/12—Discs; Drums for disc brakes
- F16D65/125—Discs; Drums for disc brakes characterised by the material used for the disc body
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D69/00—Friction linings; Attachment thereof; Selection of coacting friction substances or surfaces
- F16D2069/004—Profiled friction surfaces, e.g. grooves, dimples
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D2200/00—Materials; Production methods therefor
- F16D2200/0004—Materials; Production methods therefor metallic
- F16D2200/0008—Ferro
- F16D2200/0017—Ferro corrosion-resistant
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D2200/00—Materials; Production methods therefor
- F16D2200/0004—Materials; Production methods therefor metallic
- F16D2200/0008—Ferro
- F16D2200/0021—Steel
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D2250/00—Manufacturing; Assembly
- F16D2250/0007—Casting
Definitions
- the present invention relates to a martensitic stainless steel used for a brake disc (hereinafter referred to as a disc) as shown in FIG. 1 for use in a disc brake of a motorcycle, a car, a bicycle, etc. It relates to martensitic stainless steel for disc brakes that is hard to soften even after being kept at a high temperature for a long time due to frictional heat and has excellent tempering softening resistance (also called high temperature softening resistance) that can maintain the initial proper hardness. Things. Background art
- Disc brakes used in autopilots (motorcycles) and the like have the function of suppressing wheel rotation by the frictional force between the disc and the pad, and the temperature of the disc during braking depends on the frictional heat generated. Rises significantly.
- the thickness of the above-mentioned discs has also been reduced. As a result, there is a concern that thin disks will have a lower heat capacity, resulting in a greater temperature rise due to frictional heat during braking, and the disks will be tempered and softened, resulting in faster wear.
- 12 mass% Cr low carbon (C: 0.06 mass%) martensitic stainless steel has been mainly used as a disk brake material from the viewpoints of hardness and corrosion resistance.
- This stainless steel is usually used as it is after being processed into a predetermined shape and quenched, and its hardness is designed to be in the range of 32 to 38 in HRC (Rockwell C hardness JIS Z2245). ing.
- Japanese Patent Application Laid-Open Publication No. 2002-146482 discloses a steel sheet in which the problem of the warpage due to a rise in the temperature of the disk is improved.
- the temperature studied by this technology is up to 600 ° C, and no measures have been studied to improve the tempering softening resistance to suppress the decrease in hardness after heating.
- Japanese Patent Application Laid-Open No. 2000-224654 discloses a steel sheet having a tempering softening resistance capable of securing HRC of 30 or more even after being maintained at 530 ° C or more.
- these characteristics were insufficient for the requirement to stably secure high tempering softening resistance even at temperatures exceeding 600 ° C in recent years.
- An object of the present invention is that the tempering softening is small even after being maintained at a temperature exceeding 600 ° C, the hardness after tempering at 650 ° C is HRC of 32 or more, and further tempering at a temperature of 670 ° C.
- An object of the present invention is to provide a martensitic stainless steel for disc brakes that can secure hardness of 30 or more by HRC and has excellent tempering softening resistance even afterwards. Disclosure of the invention
- Nb and Cu finely precipitated at 500 ° C to 700 to prevent dislocation movement, softening due to strain recovery can be suppressed.
- N and Ni are added in appropriate amounts to suppress carbide precipitation at high temperatures and to confirm solid solution C.
- the present invention which has been developed based on the above findings, is as follows: C: less than 0.050 mass%, Si: 1. Omass% or less, Mn: 2. Omass% or less, P: 0.04 mass% or less, and S: OlOmass. /. Below, A1: 0.2 mass% or less, Cr: more than 11.5 to 15. Omass%, Ni 0.5 to 2. Omass%, Cu: more than 0.50 to 4. Omass%, Nb: more than 0.08 to 0.6 mass%, N 0.09 mass% Contains less than
- C less than 0.050 mass%
- Si 1.0 mass% or less
- Mn 2. Omass% or less
- P 0.04 mass% or less
- S 0. OlOmass% or less
- Cr Over 11.5 to 15.
- Omass% Ni Over 0.50 to 2.
- Omass% Cu Over 0.50 to 4.
- Omass% Nb: Over 0.08 to 0.6 mass%
- N Less than 0.09 mass%
- the present invention may be a martensitic stainless steel for a disc brake, further containing V: 0.02 to 0.3 mass% in addition to the above-mentioned component composition. 2004/005934
- the present invention is preferably a martensitic stainless steel for disc brakes containing at least one of the following (1) to (3) in addition to the above component composition.
- Ti, Zr and Ta are each 0.02 ⁇ 0.3mass%
- the steel sheet is a hot-rolled steel sheet or a cold-rolled steel sheet.
- Figure 1 Example of a brake disc for auto pie using the steel plate of the present invention Best mode for carrying out the invention
- Disk martensitic stainless steel for a brake of the present invention having the above structure, the hardness after quenching is 32 to 38 in HRC, and 6 50 ° C temperature to your Keru 32 or more HRC even after tempering It has excellent tempering and softening resistance such that it can maintain hardness of 30 or more by HRC even after tempering at a temperature of 670 ° C.
- the martensitic stainless steel for disc brakes of the present invention has characteristics of being excellent in toughness and corrosion resistance. The reason why the component composition of the martensitic stainless steel of the present invention having the above characteristics is limited to the above range will be described below.
- C is an element effective in increasing the hardness of steel after quenching.
- the content is preferably 0.015 mass% or more.
- C when C is held at a high temperature exceeding 600 ° C, C combines with Cr to form coarse Cr 23 in the case of forming a c 6, not only do not contribute to the improvement of hardness, lowering the starting point next to corrosion resistance of Hatsu ⁇ . Further, excessive addition of c reduces toughness. Therefore, the amount of C should be limited to less than 0. 050m a ss%.
- the content is preferably less than 0.05 ma SS %, and more preferably less than 0.045 mass%.
- N is an element effective in increasing the hardness of copper after quenching.
- fine Cr 2 N is formed and precipitated in the temperature range of 500 ° C to 700 ° C, and the tempering softening resistance is improved by the precipitation hardening action. Therefore, it is more effective to add N than to C in order to improve the tempering softening resistance.
- excessive addition of N causes a decrease in toughness, so it is necessary to limit the addition to less than 0.09 mass%.
- Si is limited to 1.0 mass% or less because excessive addition lowers toughness. It is preferably at most 0.3 mass%.
- Mn is an Mn S formed by combining with S, because of lowering the corrosion resistance, 2. limited to 0 m a ss%. Preferably less than 1. 0ma S s%, more preferably less than 0. 5 mass%.
- the P is an element that lowers the hot workability, and the lower the P, the better, from the viewpoint of manufacturability.
- the upper limit is 0.04 mass%.
- the content is desirably 0.02 mass% or less.
- A1 is limited to 0.2 mass% or less because excessive addition lowers toughness. It is preferably at most 0.20 mass%, more preferably at most 0.05 mass%.
- Cr is an essential component for ensuring the corrosion resistance characteristic of stainless steel, and must be contained in excess of 11.5 mass% in order to obtain sufficient corrosion resistance. From the viewpoint of obtaining more corrosion resistance, it is preferable to add 12.0 as S % or more. On the other hand, as the Cr content increases, the workability and toughness decrease. Particularly, when the Cr content exceeds 15.0 ma SS %, the toughness significantly decreases. Therefore, the upper limit is limited to 15.0 mass%. From the viewpoint of ensuring excellent toughness, it is desirable that the content is preferably less than 14.0 mass%, more preferably less than 13.0 mass%.
- Ni contributes to the improvement of temper softening resistance by delaying the precipitation of Cr carbonitride at a temperature higher than 600 ° C and maintaining the hardness of the martensite structure containing solute C in supersaturation. In addition, it improves the corrosion resistance, a characteristic of stainless steel, and is effective in improving toughness. In order to obtain these effects, it is necessary to add 0.5 mass% or more. Preferably, it is more than 0.50 mass%, more preferably 0.55: 113% or more. Further, from the viewpoint of securing sufficient temper softening resistance, it is preferable to add more than 1.0 mass%.
- it is added in excess of 0.50 mass%, and more preferably, in excess of 0.5 mass%.
- it is preferable to add 1.0 mass% or more, and more preferably 1.5 mass% or more.
- the tempering softening resistance is saturated and only the raw material cost increases.
- Nb has a strong bonding force with C and N, and precipitates NbC and NbN. Although it does not contribute to the hardness after quenching, it suppresses the recovery of the strain introduced into the martensite structure by the quenching process, and as a result, the temper softening resistance when held at a high temperature around 600 ° C To improve. In order to obtain the effect, it is necessary to add more than 0.08 mASS %, and it is preferable to add 0.10 mass% or more. On the other hand, if added in excess of 0.6 mass%, the tempering softening resistance is saturated and the toughness is reduced. Therefore, the content is limited to 0.6 thigh 83% or less. From the viewpoint of toughness, it is preferably at most 0.4 mass%, more preferably at most 0.2 mass%. • Formula (1): 0.03 ⁇ [C] + [N] -13/93 X [Nb] ⁇ 0.09
- C and N are essential elements for increasing the hardness of the steel after quenching, but NbC and NbN combined with Nb do not contribute to the improvement of hardness. Therefore, when controlling the hardness of the steel after quenching, the effect of C and N is calculated by subtracting the amount consumed for precipitates from C and N in the steel, [C] + [N] —13 / 93X [Nb]).
- the value of the intermediate section is less than 0.03 lower than the hardness of HRC 32, whereas, therefore c hardness exceeds 0.09 is to exceed 38 in HRC, proper hardness after quenching as a disk brake application In order to set the HRC to 32 to 38, limit the intermediate term in equation (1) to 0.03 to 0.09.
- Equation (2) is an evaluation parameter for quenching stability.
- 90% or more austenite phase should be generated when heated to 900 ° C to 1000 ° C, and it should be transformed into martensite when air cooled. is necessary.
- the austenite phase is highest at around 1000 ° C, and the amount of austenite phase decreases both above and below 1000 ° C.
- the temperature range in which the austenite phase is formed in an amount of 90% by volume or more is narrowed, and fluctuations in the quenching temperature during the manufacturing process cause sufficient baking. It will fall out of the appropriate hardness range without entering.
- the quenching temperature be as low as possible because the higher the quenching temperature, the higher the heat cost and the longer the time required to raise the temperature.
- the HRC of quenching at 900 ° C is 32 or more.
- V is an element effective to form and precipitate fine carbonitrides and improve the tempering softening resistance, preferably 0.02 mass% or more, more preferably 0.10 mass%.
- the above can be added. However, if added in excess of 0.3 mass%, the toughness decreases, so it is preferable to set the upper limit to 0.3 mass %.
- Mo Co is an effective ingredient in improving corrosion resistance of can be added thereto Re 0. 02ma S s% or more as necessary.
- Mo like Ni, slows down the precipitation of Cr carbonitrides and maintains the hardness of the martensitic phase containing C in supersaturation. This also has the effect of improving the tempering softening resistance. From the viewpoint of further improving the corrosion resistance, it is preferable to add 0.5 mass% or more of each. If it is less than 1.5%, sufficient corrosion resistance can be obtained. On the other hand, when the content of each element exceeds 2.0 mass S %, the effect of improving corrosion resistance is not only saturated, but also the toughness is reduced. Therefore, the upper limit is preferably 2.0 mass%.
- Ti, Zr and Ta are elements that form and precipitate fine carbonitrides and improve the softening resistance to tempering.If necessary, each can be added in an amount of 0.02 mass% or more. . However, since the toughness when added in excess of 0. 3niass% decreases, preferably the upper limit, respectively 0. 3m aS s%.
- B and Ca have the effect of increasing the toughness of the steel when added in trace amounts, and it is preferable to add 0.0005% by mass or more of each, if necessary. However, even if it is added in excess of 0.0050111 3%, not only does the effect become saturated, but also the corrosion resistance is reduced, so the upper limit is preferably 0.0050mass%.
- the martensitic stainless steel of the present invention comprises Fe and unavoidable impurities other than the above components.
- the unavoidable impurities may contain small amounts (0.01% SS SS or less) of alkali metals such as Na, Ba, La, Y, and Hf, alkaline earth metals, rare earth elements, and transition metals. It does not hinder the effect of the present invention at all.
- the steel of the present invention generates an austenite phase of 90% by volume or more when heated to 900 ° C to 1000 ° C, and when the steel is air-cooled, It is necessary to transform the martensite.
- the structure of the martensitic stainless steel for a disc brake of the present invention is 90 volumes. /. It is desirable to use the above martensite phase and the remaining ferrite phase. 90 volumes of martensite phase. If it is less than / 0 , the soft ferrite phase becomes too large, and it is difficult to obtain a desired hardness.
- the method for producing the steel of the present invention is not particularly limited, and a generally known method generally employed for producing a martensitic stainless steel can be applied as it is.
- steel containing the above essential components and components added as necessary is melted in a converter or an electric furnace, etc., and is subjected to vacuum degassing (RH), VOD (Vacuum Oxygen) Decarburization)
- RH vacuum degassing
- VOD Vauum Oxygen
- a method of performing secondary refining by a refining method such as ADF (Argon Oxygen Decarburization) is preferred.
- the smelted steel can be made into a steel material (slab) by a known method such as a continuous casting method or an ingot slab rolling method, but from the viewpoint of productivity and quality, the continuous casting method is used.
- the obtained steel material is heated from 1100 to 1250 ° C, then hot-rolled at a finishing rolling temperature of 800 to 1100 ° C, wound up in the temperature range of 600 to 900 ° C, and the thickness of the sheet is 3 to 8 Orchid hot rolled steel strip.
- This hot-rolled steel strip is annealed in a batch furnace such as a box annealing furnace at 650 to 900 ° C for 4 to 20 hours, and then processed into sheets as necessary to be used as a disk material. If necessary, the hot-rolled steel strip may be subjected to descaling treatment such as pickling and shot plast.
- the disc material obtained as above is then punched into a disc mold, heated to a temperature of 900 ° C to 1000 ° C, and then quenched by air cooling or cooling at a higher speed. Further, if necessary, descaling and painting are performed, and then the sliding surface with the brake pad is mechanically polished to improve the aesthetics and plate thickness accuracy to produce a disk product as shown in Fig. 1.
- the martensitic stainless steel of the present invention obtained as described above can be used for brake discs for bicycles, automobiles, snowmobiles, etc., in addition to brake discs for motorcycles.
- the disc for bicycle disc brakes has a thickness of about 2 mm, so the hot-rolled steel strip obtained after annealing and pickling as described above can be used in a reverse rolling mill such as Sendzimir.
- the material is annealed at a temperature of 600 to 900 ° C if necessary, and further, if necessary, pickled to obtain a disk material. Thereafter, the disc material can be made into a product through the same process as the hot-rolled steel product.
- the above test materials were heated and held at 1000 ° C for 10 minutes, then quenched by air cooling, and then tempered at 650 ° C for 1 hour.
- 70mm x 150mm x sheet thickness test pieces are cut out one by one, and the test surface (one side of the test piece) is wet-polished with # 800 emery abrasive paper, and then 8 hours in accordance with JIS Z2371.
- a salt spray test was performed on the test surface, and the number of starting points on the test surface was measured.
- the evaluation of corrosion resistance was as follows: no start point, 1 to 4 start points, and X, 5 or more start points. In addition, it can be evaluated that there is a practical problem in corrosion resistance at the starting point of 5 or more. .
- the toughness was determined by heating and holding the above test material at 1000 ° C for 10 minutes, then air cooling, quenching, and tempering at 650 ° C for 1 hour.
- a sample of three sub-size Charpy impact test specimens (thickness: 10 mm, width: 5 mm (thickness of hot-rolled sheet), length: 55 mm) conforming to the standard is sampled and subjected to a Charpy impact test (JIS Z2242) at 25. ), Measured the Charpy impact value, and averaged the values. If the Charpy impact value is 50 J / cm 2 or more, it can be evaluated that there is no practical problem.
- the measurement results of the above tests are also shown in Tables 1-4.
- the steels of Tables 1, 2 and 3 that meet the criteria of the present invention (Nos. 1 to 49) were all 900 and 1000 ° C
- the hardness after quenching at HRC is within the appropriate range of 32 to 38 at HRC, and the hardness after quenching from 1000 ° C and tempering at 650 ° C is 32 or more at HRC, and 670 ° C
- the hardness after tempering in HRC is 30 or more in HRC, and the Charpy impact value is 50 J / cm 2 or more. It also has good corrosion resistance in saltwater fog.
- the steel shown in Table 4 which do not meet the criteria of the present invention (No.
- the hot-rolled steel sheet of the martensitic stainless steel of the present invention is as follows. It can be seen that the material has excellent properties as a disc brake material.
- Example 2 Next, the characteristics of the cold-rolled steel sheet were investigated. The 5 mm hot-rolled annealed specimen of steel No. 1 in Table 1 in Example 1 was cold-rolled to a thickness of 1.5 mm, 750 ° C for 1 minute, air-cooled, and then annealed. And then mixed acid at 60 ° C
- the hardness after tempering at 670 was 32 on the HRC. Further, the Charpy impact value was 85 J / cm 2 , and no corrosion was observed after the corrosion resistance test with salt water fog, and the corrosion resistance was good. Based on these results, the cold rolled steel sheet of martensitic stainless steel of the present invention is similar to the hot rolled steel sheet in the disc brake. It was confirmed that the material had excellent characteristics as a disc material. Industrial applicability
- the present invention by controlling the elemental composition of the element within an appropriate range, it does not significantly soften even after being maintained at a temperature exceeding 600 ° C. 650. Martensite for disc brakes with excellent tempering softening resistance, which can secure hardness of 32 or more by HRC even after tempering C and lh, and more than 30 by HRC even after tempering at 670 ° C and lh. G stainless steel can be obtained.
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- Organic Chemistry (AREA)
- General Engineering & Computer Science (AREA)
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- Heat Treatment Of Sheet Steel (AREA)
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Description
Claims
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US10/546,248 US8357247B2 (en) | 2003-04-28 | 2004-04-23 | Martensitic stainless steel for disk brakes |
EP04729283A EP1621644B1 (en) | 2003-04-28 | 2004-04-23 | Martensitic stainless steel for disc brake |
US13/200,933 US20120048662A1 (en) | 2003-04-28 | 2011-10-05 | Martensitic stainless steel for disc brakes |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2003124027 | 2003-04-28 | ||
JP2003-124027 | 2003-04-28 |
Related Child Applications (2)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US10/546,248 A-371-Of-International US8357247B2 (en) | 2003-04-28 | 2004-04-23 | Martensitic stainless steel for disk brakes |
US13/200,933 Division US20120048662A1 (en) | 2003-04-28 | 2011-10-05 | Martensitic stainless steel for disc brakes |
Publications (1)
Publication Number | Publication Date |
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WO2004097058A1 true WO2004097058A1 (ja) | 2004-11-11 |
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Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
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PCT/JP2004/005934 WO2004097058A1 (ja) | 2003-04-28 | 2004-04-23 | ディスクブレーキ用マルテンサイト系ステンレス鋼 |
Country Status (5)
Country | Link |
---|---|
US (2) | US8357247B2 (ja) |
EP (1) | EP1621644B1 (ja) |
KR (1) | KR100698395B1 (ja) |
CN (1) | CN100371487C (ja) |
WO (1) | WO2004097058A1 (ja) |
Families Citing this family (30)
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US8357247B2 (en) * | 2003-04-28 | 2013-01-22 | Jfe Steel Corporation | Martensitic stainless steel for disk brakes |
ES2744858T3 (es) * | 2006-10-05 | 2020-02-26 | Jfe Steel Corp | Discos de freno con excelente resistencia a ablandamiento por revenido y tenacidad |
CN101538686B (zh) * | 2008-03-21 | 2012-01-11 | 宝山钢铁股份有限公司 | 一种结构件用马氏体沉淀硬化不锈钢及其制造方法 |
WO2009131248A1 (ja) * | 2008-04-25 | 2009-10-29 | Jfeスチール株式会社 | 低炭素マルテンサイト系Cr含有鋼 |
ES1069143Y (es) * | 2008-11-27 | 2009-05-01 | Aloy Jordi Nadal | Disco de freno autoventilado |
KR100935882B1 (ko) * | 2009-07-22 | 2010-01-11 | 다산폴리텍 주식회사 | 고탄소 합금주철재 브레이크 디스크 |
CN102719761B (zh) * | 2011-12-29 | 2013-11-27 | 通裕重工股份有限公司 | 轮盘锻件及制造工艺 |
US10520052B2 (en) * | 2012-01-18 | 2019-12-31 | Shimano Inc. | Bicycle disc brake rotor |
UA111115C2 (uk) | 2012-04-02 | 2016-03-25 | Ейкей Стіл Пропертіс, Інк. | Рентабельна феритна нержавіюча сталь |
KR101463315B1 (ko) * | 2012-12-21 | 2014-11-18 | 주식회사 포스코 | 경도와 저온 충격특성이 우수한 스테인리스 열연강판 |
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US10047417B2 (en) * | 2015-03-11 | 2018-08-14 | Aktiebolaget Skf | Continuous caster roll for a continuous casting machine |
CN106319379A (zh) * | 2015-07-01 | 2017-01-11 | 上海添御石油设备科技有限公司 | 一种石油压裂车的压力泵阀箱用不锈钢材料 |
KR101899635B1 (ko) * | 2015-12-11 | 2018-10-04 | 주식회사 포스코 | 부착형 고망간강 브레이크 디스크 |
ES2862309T3 (es) * | 2016-04-12 | 2021-10-07 | Jfe Steel Corp | Lámina de acero inoxidable martensitico |
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AT526715A1 (de) * | 2022-11-16 | 2024-06-15 | Hascic Ing Daniel | Bremselement |
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JP2001220654A (ja) | 1999-11-30 | 2001-08-14 | Nippon Steel Corp | 焼戻し軟化抵抗の高いディスクブレーキ用ステンレス鋼 |
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- 2004-04-23 US US10/546,248 patent/US8357247B2/en active Active
- 2004-04-23 KR KR1020057016247A patent/KR100698395B1/ko active IP Right Grant
- 2004-04-23 WO PCT/JP2004/005934 patent/WO2004097058A1/ja active Application Filing
- 2004-04-23 EP EP04729283A patent/EP1621644B1/en not_active Expired - Lifetime
- 2004-04-23 CN CNB2004800102086A patent/CN100371487C/zh not_active Expired - Lifetime
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JP3422864B2 (ja) * | 1995-01-19 | 2003-06-30 | 新日本製鐵株式会社 | 加工性の優れたステンレス鋼およびその製造方法 |
US5979614A (en) * | 1996-09-25 | 1999-11-09 | Nippon Steel Corporation | Brake disc produced from martensitic stainless steel and process for producing same |
EP1106705A1 (en) * | 1999-11-30 | 2001-06-13 | Nippon Steel Corporation | Stainless steel for brake disc excellent in resistance to temper softening |
JP2001220654A (ja) | 1999-11-30 | 2001-08-14 | Nippon Steel Corp | 焼戻し軟化抵抗の高いディスクブレーキ用ステンレス鋼 |
WO2002018666A1 (fr) * | 2000-08-31 | 2002-03-07 | Kawasaki Steel Corporation | Acier inoxydable martensitique a faible teneur en carbone et son procede de production |
JP2002146489A (ja) | 2000-08-31 | 2002-05-22 | Kawasaki Steel Corp | 耐熱性に優れた低炭素マルテンサイト系ステンレス鋼板 |
EP1199374A1 (en) * | 2000-10-18 | 2002-04-24 | Shimano Inc. | A novel stainless steel for a disc brake rotor |
JP2002146482A (ja) | 2000-11-01 | 2002-05-22 | Nisshin Steel Co Ltd | 耐反り性を改善したディスクブレーキ用鋼板およびディスク |
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Also Published As
Publication number | Publication date |
---|---|
EP1621644A4 (en) | 2007-05-23 |
KR100698395B1 (ko) | 2007-03-23 |
US20060113008A1 (en) | 2006-06-01 |
US8357247B2 (en) | 2013-01-22 |
CN1774520A (zh) | 2006-05-17 |
EP1621644A1 (en) | 2006-02-01 |
US20120048662A1 (en) | 2012-03-01 |
CN100371487C (zh) | 2008-02-27 |
KR20050107595A (ko) | 2005-11-14 |
EP1621644B1 (en) | 2012-08-08 |
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